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Light scattering spectroscopy of pulydimethylsiloxane-toluene gels
J.P. Munch, P. Lemaréchal, S. Candau, J. Herz
To cite this version:
J.P. Munch, P. Lemaréchal, S. Candau, J. Herz. Light scattering spectroscopy of pulydimethylsiloxane- toluene gels. Journal de Physique, 1977, 38 (12), pp.1499-1509. �10.1051/jphys:0197700380120149900�.
�jpa-00208725�
LIGHT SCATTERING SPECTROSCOPY OF PULYDIMETHYLSILOXANE-TOLUENE GELS
J. P.
MUNCH,
P.LEMARÉCHAL,
S. CANDAULaboratoire
d’Acoustique
Moléculaire(*),
UniversitéLouis-Pasteur, 4,
rueBlaise-Pascal,
67070Strasbourg Cedex,
Franceand J. HERZ
Centre de Recherches sur les
Macromolécules, C.N.R.S., 6,
rueBoussingault,
67083Strasbourg Cedex,
France(Reçu
le1 er juillet 1977, accepté
le 18 août1977)
Résumé. 2014 La fonction d’autocorrélation de la lumière diffusée a été mesurée pour des gels de
polydiméthylsiloxane-toluène
formés soit pargonflement
de réticulats permanents, soit par dissolu- tion de macromolécules linéaires à des concentrations moyennes. Dans les deux cas le coefficient de diffusioncoopératif
varie avec la concentration enpolymère
selon une loi depuissance
avec un exposantplus
élevé que celui qui avait été obtenuprécédemment
pour des systèmespolystyrène-
benzène. Par ailleurs, il est montré que les modules de
compression
uniaxiale n’obéissent plus à deslois d’échelle simples avec la concentration pour des réseaux gonflés par un liquide moins bon solvant que celui dans lequel a été réalisée la réticulation.
Abstract. 2014 The autocorrelation function of scattered
light
has been measured forpolydimethyl-
siloxane-toluene
gels
formed either byswelling
permanent networks or by dissolving linear macro-molecules at moderate concentrations. In both cases, the cooperative diffusion constant varies with concentration according to a power law with an exponent larger than that obtained
previously
forpolystyrene-benzene
systems. On the other hand, it is shown that uniaxial compression moduli donot obey simple
scaling
laws with the equilibrium concentration for networks swollenby
a diluent ofless quality than the solvent in which the
crosslinking
has been made.Classification
Physics Abstracts 61.40K201362.00201366.10
1. Introduction. - Traditional methods for measur-
ing
the viscoelasticproperties
ofgels generally depend
on mechanical devices. It has been shownrecently
thatoptical mixing spectroscopy yields
valuable information
concerning
thehydrodynamic properties
of bothpermanent
swollen networks[1-8]
and semi-dilute or concentrated
polymer
solutions[8- 11].
A theoretical model has been
proposed
whichassumes that the
light
scattered from agel
arises from collective excitations of the network[1, 12, 13].
From this
model,
the correlation function of thepolarized
scatteredlight
for alongitudinal
fluctuation of wavevector K ispredicted
to have the form ofan
exponential decay.
Thedecay
rate isgiven by
T =
De K2
whereDp
is thecooperative
diffusionconstant of the chains of the network.
On the other
hand,
acorpuscular
model has beenproposed by
Mc Adam et al.[2]
and Carlson et al.[3,
(*) Equipe de Recherche Associée au C.N.R.S.
4],
which assumes that each macromolecule in thegel
state behaves as aharmonically
boundparticle executing independent
Brownian motion about astationary
mean. Theresulting theory predicts
anon-exponential intensity
autocorrelation functiongiven
in terms of a chain elastic constant and the conventional translational diffusion coefficient.In
previous
papers, we havereported
autocorre-lation measurements on benzene-swollen model net-
works of
polystyrene
and shown that thehydro- dynamic
model fits the observed data. Thecooperative
diffusion constant of
gels
has beeninvestigated
asa function of the method of
synthesis
of the networks and their characteristics.In
a firstattempt,
we have assumedideality
ofnetworks,
i.e. absence of structure defects such aspendant chains, cycles,
orentangle-
ments, and
interpreted
the results obtained within the framework of the rubberelasticity theory [5-7].
From this
analysis,
we were led to the conclusionthat the so-called memory term, which relates the dimension of the elastic chain in the swollen state and the reference swollen state
respectively,
isstrongly
Article published online by EDP Sciences and available at http://dx.doi.org/10.1051/jphys:0197700380120149900
dependent
on thefunctionality
of thecross-linking
agent.
Recently,
we havereanalyzed
the databy allowing
the presence ofentanglements trapped
between two permanent
junction points
and assum-ing, according
to asuggestion
of deGennes,
that the average distance between the cross-links wasin the first
approximation
identical to thedynamical screening length [8].
Thisassumption implies
thatboth the
cooperative
diffusion constant and theextensional modulus should
obey scaling
laws withswelling equilibrium
concentration. Such behaviour has beeneffectively
observed forpolystyrene-benzene gels.
Most of the networks
investigated
wereprepared
by
anionicblock-copolymerization
of styrene withsmall.
amounts ofdivinylbenzene.
In this type ofnetwork,
each linear chain element is connected with two different branchpoints
constitutedby polydivinylbenzene
nodules. The chain elements have the characteristicsharp
molecularweight
distribution ofpolymers prepared by
anionicpolymerization.
A drawback of the method used here is that the actual
functionality
of the crosslinks is unknown.In the present paper we report measurements of the
cooperative
diffusion constant of ahomologous
series of
polydimethylsiloxane (PDMS)
networksswollen in toluene. In many respects these
gels
arevery different from the
polystyrene
networks investi-gated previously :
- Both the average molecular
weight
of the elastic chains and thefunctionality
of thepermanent
cross- links are knownparameters.
- Branch
points
are formedby single pluri-
functional molecules instead of nodules of
appreciable
dimensions as was the case for the branch
points
ofthe
polystyrene
networks described above.- The elastic
properties
of PDMS networks arevery different from those of
polystyrene
networkssince the
glass
transition of PDMS occurs at a tempe-rature far below room
temperature ( - 120 °C).
- In all
synthesis
the precursorpolymer
concen-tration
during
network formation was muchhigher
than the
equilibrium
concentration of the swollen networks. Thus the networks do not contain any macropores.- The
swelling degree
of the PDMS networks in toluene isconsiderably
lower than that ofpolysty-
rene networks swollen at
equilibrium
in benzene.2. Theoretical. - The essential feature of a
gel
isthat each macromolecule linked to the network
by
both chain-ends is nolonger
free to diffusethrough
the whole network structure but is confined to a
region
of the networkcompatible
with the number of effective crosslinks. Two differentapproaches
have been used to described the viscoelastic behaviour of
gels.
Mc
Adam, et
al.[2], Carlson, et
al.[3, 4]
haveproposed
asimple
model ofscattering
moleculesin the
gel
state which assumes each molecule to beharmonically
bound andexecuting
brownian motion around astationary
meanposition. Upon application
of the Ornstein and Uhlenbeck distribution function for such a
particle [14],
Carlson and Fraser[3]
havederived an
expression
for the non-normalizedoptical
field autocorrelation function
G(l)(T) :
.where I is the average
intensity
of thefield,
D is thetranslational diffusion constant of the
particle,
Kis the
scattering
wavevector and y(sec-l)
the ratioof the chain elastic constant k
(dyne/cm)
to the fric-tional constant
f (dyne s/cm).
From
equation (1)
it follows that the lineprofiles
in a
self-beating experiment
will not besimple
lorent-zian with a linear
relationship
between line-width andK2. Furthermore,
the initialamplitude
of thenormalized
intensity
autocorrelation functiong(2)(O)
will have a
K-dependent
value which isalways
lessthan
2,
in contrast to thefreely diffusing particle
whose
g(2)(O)
= 2. In the derivation ofequation (1),
uncorrelated
Rayleigh scattering
has beenassumed, neglecting
the presence of alarge component
of staticscattering by
thegels
which is due to micro-scopic inhomogeneities.
Then in a later paper[4]
Wun and Carlson have included in the
intensity
an additional term to account for the additional static
scattering
which contributes to thelowering
of the initial
amplitude
ofg(2)( -r).
In the second
model, developed by Tanaka, et
al.
[1 ],
and de Gennes[12],
thegel
is considered as acontinuum and the
light scattering
is assumed to arise fromlongitudinal
deformation modes of the network. The deformation of the swollen network has been shown toobey
a diffusionequation
andthe correlation function of the
polarized
scatteredlight
isgiven by :
The
cooperative
diffusion constantDe
of the chains of the network isgiven by :
1"B il)’B
wnere p (clyne/cm-) is tne longitudinal compressionai modulus and 0
(dyne s/cm4)
the frictional force per unit volume of the network as it moves with unitvelocity
relative to thesurrounding liquid.
p and 0 are
given respectively by [ 12] :
- , ,
vo
being
numberdensity
of network chains in the swollenstate, 17
theviscosity
of theswelling liquid
and
Rh hydrodynamic
radius of one chain.By combining equations (3), (4)
and(5)
one obtains :where
Df
stands for the translational diffusion coefficient for a dilute solution of free macromoleculeshaving
thehydrodynamic
radiusRh.
This
hydrodynamic theory
leads to results whichare
quite
different from those derived from the har-monically
boundparticle model,
since itpredicts
an
exponential
timedecay
of the autocorrelation function of theoptical
field with a linearrelationship
between
decay
rate andK2.
UncorrelatedRayleigh scattering
has been assumed so that no account has to be taken of the staticscattering
due tospatial
non-randomness of the
crosslinking.
This additionalcomponent
acts as a localheterodyning
source.Therefore,
ifIo
stands for theintensity
of the staticcomponent (including
dusttrapped
in thenetwork)
and
7g
for theintensity
scattered fromlongitudinal fluctuations,
the normalizedintensity
autocorrelation function isgiven by [15] :
When
Io > I,,, equation (7)
reduces to :In
previous
papers, we have shown thatg2(z) obeys equation (8)
forpolystyrene-benzene gels [7].
According
toequation (6),
thecooperative
diffusionconstant
depends
on the dimension of the elastic chainsjoining
two crosslinks which in tumdepends
on the
swelling equilibrium
concentrationCe.
TheFlory theory
ofswelling predicts
thefollowing dependence
ofCe
on the molecularweight Me
ofthe elastic chain
[16]
However,
this result has been derived from an expres- sion of the free energy which has been shown to be incorrect and which leads to correct resultsonly
in dilute solutions
[17].
A new
approach,
based onscaling
law theories has beenrecently proposed, describing
static anddynamical properties
of both dilute and semi-dilute solutions[13, 17, 18].
Semi-dilute solutions can be considered as net-, t works with a finite lifetime. The average distance between
neighbouring
crosslinks isgiven by
thescreening length ç
whichdepends only
on the concen-tration, according
to thefollowing scaling
law[13]
Therefore,
the diffusion constantD,
isgiven by
In swollen networks at the
equilibrium
state, the average distance betweenneighbouring
cross-links
depends
on theswelling equilibrium
concen-tration
Ce.
De Gennessuggested
that this distance isgiven
as in the case ofinterpenetrated
solutionsby
the
screening length j.
Thisassumption implies
that :The
equilibrium
concentration isgiven
in the firstapproximation by :
where
Me represents
the molecularweight
of theelastically
effective chainsconnecting
twojunction points regardless
of their nature,entanglements
orpermanent crosslinks. For ideal networks
prepared
from a precursor
polymer
of known molecularweight M p’ ç
isequal
to the radius ofgyration RF
of the precursor
polymer.
Therefore :where C* is the cross-over concentration between dilute and semi-dilute
regions
for a solution of macromolecules of molecularweight Mp.
Combination of
equations (12)
and(13)
leadsto the
following
concentrationdependence
ofDc
Then,
one canpredict
the sameexponent
for bothscaling
lawsD,,
=f (C )
andDe
=f (Ce)
relative tosemi-dilute solutions and swollen
networks,
res-pectively.
This result has been verifiedexperimentally
in
polystyrene gels [8].
It is also
interesting
to consider the concentrationdependence
of thecompressional
modulus E. InFlory’s theory, E
isproportional
to the numberdensity
ofelastically
effective chains in thedry
state
[16].
As aconsequence, E
ocCe2.
On the other
hand, scaling
lawtheory predicts
that E is
proportional
to the numberdensity
ofelastic chains in the swollen state,
resulting
in thefollowing scaling
law for E[13]
Such a
dependence
of E onCe
has been observed inpolystyrene
networks swollenby
benzene.3.
Expérimental.
- 3.1 PREPARATION AND CHA- RACTERISTICS OF SAMPLES. -Polydimethylsiloxane
networks were obtained
by
the addition reaction of(a - co) dihydropolydimethylsiloxane
precursorpolymers
withplurifunctional allyloxy compounds, using H2PtC’,,
as acatalyst.
The method has been described earlier[19].
Thesecrosslinking
reactionswere carried out in the presence of toluene at 60 OC.
Triallyloxy-1,2,3
propane,tetraallyloxyethane,
andbis
allyloxy-3 dimethylallyloxy-2,2
propane oxide[20]
were used as
3, 4
and 6 functionalcrosslinking
agents.The precursor
polymers
were chosen in a molecularweight
range between 4 500 and 17 000.The volume
swelling degree
of the networks atequilibrium
has been determined with an accuracy of about5 %, using
aprocedure already
described[21].
The
experimental technique
and theapparatus [22, 23]
used for unidirectionalcompression
measurements have also been described elsewhere[24].
All compres- sion measurements were carried out on networks swollen atequilibrium
in toluene at small deformation ratios 0.8 A 1.In table 1 are listed the
network-samples
and theircharacteristics.
Table II shows the molecular
weights Mn
of thelinear PDMS
samples
used in ourexperiments,
determined
by
chemicalendgroup analysis. Sample
1is a linear PDMS obtained
by
an anionicpolyme-
rization method
(1). Samples
2-5 are(a - co) hydro- genosilane polydimethylsiloxanes (2),
which have been used for thepreparation
of networks.TABLE 1
PDMS swollen in toluene
(a)
e) The networks have been prepared in toluene at 70 °C at a
concentration of 83 % .
(b) Number average molecular weight of the precursor polymer
determined by endgroup analysis.
(C) Functionality of the crosslinking agent.
(a) Data of Belkebir Mrani et al. [24]. (E is related to the para- meter G * of the authors through the relationship E = G *
q¡Õ 1/3,
where qio is the swelling equilibrium ratio.)
(e) Determined from light scattering spectroscopy.
(1) The authors are grateful to Dr. S. Boileau who has prepared
this high molecular weight polymer.
(2) These polymers were prepared by the Silicon Division of Rhône-Poulenc.
TABLE II Linear PDMS
(1) The weight average molecular weight, the radius of gyration
and the second virial coefficient in toluene, have been determined
by conventional light scattering.
We have no exact information
concerning
thepolydispersity
of thesamples. However,
ananalysis
of the autocorrelation function of the
photocurrent, performed by
the method of cumulants[25, 26, 15]
showed that the
polydispersity
index(ratio
ofweight
average molecular
weight
to the number average molecularweight)
does not exceed 1.3. Such a value ofMw/Mn
is notnegligible,
but thispoint
is not ofgreat importance
for the purposes of ourstudy.
3. 2 LIGHT SPECTROSCOPY. - The spectrometer and autocorrelator for
intensity
autocorrelation measure- ments have been described before[15].
Thelight
source was an argon ion laser
(Spectra Physics
Model
165)
with awavelength
of 488 nm. The cubicshaped gel samples (-
1cm3)
wereput
into standardglass
cellscontaining
an excess ofswelling liquid.
The scattered
light
was collected at apre-determined angle by
a lens aperturesystem
and focused onto the sensitive part of aphotomultiplier (ITT
FW130)
cathode. The
photocurrent
wasanalyzed
afterpassing through
anamplifier-discriminator by
a 24-channeldigital
autocorrelator(Precision
Devices andSystems,
Ltd Malvem
system 4300).
The data from the corre-lator were
analyzed by
the method of cumulants[25, 26, 15]
which allows for a distribution ofdecay
rates
G (F)
andmakes
itpossible
to calculate the averagedecay rate F
and the second-order norma-lized moment
(Jl2/f2)
about the mean of f.We have mentioned in the theoretical section that the
intensity
scattered fromlongitudinal
fluctua-tions of swollen networks must be
heterodyned
tosome extent
by
the staticcomponent
due to micro-scopic heterogeneities. Furthermore,
nospecial
carehas been taken to eliminate dust in the
reagents
and the solvent used for the networksynthesis ;
the dusttrapped
in thegel
will also contribute to theheterodyn- ing.
As a consequence, the initialamplitude 1 gl2@(0) 1
of the normalized
photocount clipped
correlation function must be lower than that obtained forpolymer
solutions in an
homodyne self-beating experiment,
which in
practice
is about 1.75 on account of incom-plete spatial
coherence.As a matter of
fact,
it turns out that for all theinvestigated gels, gk2(O) 1
= 1.01-1.1. These verysmall values
of 1 gL2)(O) indicate
that theheterodyne
component
dominates thehomodyne component
and henceequation (8)
mustapply.
In order to check this last
point
we have measured the autocorrelation function obtainedby mixing
the scattered
signal
with an externalsignal.
In thescattering angle
range of60-900,
the initialamplitude
of the normalized autocorrelation function has been found to be reduced
further,
but thedecay
time isnot affected.
Alternatively,
a two hundred-channel real timewave
analyzer (Saicor
Model SAI 21B)
was used tomeasure the spectrum of the
photocurrent
from thephotomultiplier.
In all cases where theexperimental
data were described
by
asingle decay
rater,
bothwave
analyzer
and autocorrelator led to identical values of r within 2%.
All the measurements were
performed
at roomtemperature (23 OC).
Thepolydimethylsiloxane
net-works swollen
by
toluene were allowed to standat room
temperature
for at least oneday
to allow thesample
to stabilize in the cell. Thestability
couldbe checked
by monitoring
theintensity
of the DCcomponent.
The solutions of PDMS in toluene were made dust free
by centrifugation (15
000rev/min.).
Forconcentrations
larger
than 0.5 x10- 2 g. cm- 3,
theFIG. 1. - Semi-dilute solutions of linear PDMS Mw = 6 x 106 in toluene. a) c=3 x 10-2 g.cm-3 ; b) c=1.42x 10-2
g.cm-3 ;
0 A Scattered signal alone ; 1 à Scattered signal mixed with
external oscillator.
solutions of
sample
1 were too viscous to allow sucha
procédure ; therefore,
the solutions were madewith a
previously
clarified toluene.However,
somedust remains in the solutions
giving
rise to a hetero-dyning
of the scatteredsignal.
The rate of hetero-dyning
varies with both concentration andscattering angle,
as illustrated infigure
1. Thispoint
is of greatpractical importance
since it could lead to an incorrectanalysis
of the concentrationdependence
and wave-vector
dependence
of thedecay
rate of the correlation function. For this reason we have checked the scatter-ing mode (homodyne
orheterodyne) by mixing
thescattered
signal
with an externaloscillator, using
aMichelson
type
interferometer. In all cases where theheterodyning
from dust wasonly partial,
we havemeasured the
decay
rateby using
the Michelsongeometry.
Table IIIgives
thescattering
modesexperimentally
observed for the different concen-trations.
4. Results. - 4. 1 SOLUTIONS OF PDMS IN TOLUENE.
- In
polymer
solutions ofgiven
concentration c, theshape
of the correlation function for scatteredlight g(i)
and the Kdependence
of thedecay
rate rdepend
on thefollowing
four parameters : the radius ofgyration RF
of thechain,
the cross-over concen-tration
c*,
thescattering
wavevectorK,
and the minimum wavevectorKm;n
at which the relaxation time iK of alongitudinal
mode of wavevector K isequal
to the relaxation timeT,
forcomplete
disen-tanglement
of one macromolecule.FIG. 2. - Various regimes for longitudinal fluctuations of wave vector K in solutions of polymer in a good solvent.
TABLE III
Scattering
modesfor
solutionsof sample
1(Mw
= 6 x106)
in tolueneBecause of the
large
ranges ofconcentration,
molecularweight
andscattering
wavevector investi-gated
in ourexperiments,
we have obtained data in variousregimes
definedby
the relative values of theseparameters.
For theclarity
of the discussionwe have
reproduced
infigure
2 thediagram given by
de Gennes
[13] showing
the range of concentration and momentum transfer for thepredicted
existenceof the different types of modes. One can summarize the
possible experimental
situations on thefollowing
way.
4.1.1 Dilute
regime
c c*. -a) Region II
g(i)
isexponential
Do
is the self diffusion of one chainb)
Region
IIIg(i)
is nonexponential
r is the average
decay
rate. Oneprobes
inner modesof a
single
chain.4.1.2 Semi-dilute
regime
c > c*. -a) Region
1g(il
isexponential
De
is thecooperative
diffusion constant in thegel regime
b) Région
II’g(i)
isexponential
Dfree
is the diffusion constant in thedisentangled regime
The différence between
D free
andDe
amounts toa
change
ofprefactors.
c) Region
III’g(i)
is nonexponential r
ocK3.
One
probes
inner modes within a coherencelength.
The behaviour which is of interest for a
quantitative comparaison
betweencooperative
modes of swollenpermanent
networks and semi-dilute solutions is the concentrationdependence
ofDe
in theregion
I.In order to determine
accurately
the concentrationdependence
of the diffusion constant in bothregions
1and
II,
one must determine the ranges ofscattering
wavevector where the two
following
conditions arefulfilled :
i)
the autocorrelation functiondecays exponentially ; ii)
thedecay
rate follows aK2 depen-
dence. It is not easy to characterize with accuracy the range of K values where the autocorrelation function
departs
from anexponential.
On the otherhand,
theprocedure
which consists ofdetecting
adeparture
from the K2dependence
of thedecay
rateobtained
by fitting g(z)
to anexponential
isquite
sensitive.
Figure
3 shows the ranges of K values where r varies likeK2,
for differentpolymer
concen-trations. In these
domains,
ananalysis using
themethod of cumulants shows that the correlation function is well described
by
asingle exponential,
except for the dilute solutions where a
slight
distri-bution of
exponentials
occurs. The averagedecay
rate of this distribution is about the same
(within
3% )
as the
decay
rate determinedby
forcefitting
asingle exponential and
the value of the second-ordermoment (/12/r2)
is about - 0.1. Such a value of/12/r2
would indicate apolydispersity
indexM,,IM. - 1.3. However,
one mustpoint
out thatthe measurements have been
performed
at lowscattering angles (7°
915°)
where the effect of thenon-negligible
acceptanceangle
for scatteredlight
may lead to an overestimation ofMw/Mn.
The solid line
Kç
= 1(where ç
has been calculated fromD/Do
=RF/ç) reported
onfigure
3 represents the transition line fromregions
II and 1 toregions
IIIand III’
respectively.
Theexperimentally
observeddeviation of T from the K2
dependence
indicatesthe existence of the concentration
dependent
corre-FIG. 3. - Semi-dilute solutions of linear PDMS MW=6 x 106 in
toluene. Q c=0.47 x 10-4 g.cm-3 ; x c=4.5 x 10-4 g.cm-3 ; o c = 9 x 10 - 4 g. cm - 3;
+ c = 0.18 x 10-2 g.cm-3 ;
Z c = 0.36 x 10-2 g.cm-3 ; 0 c = 0.72 x 10-2 g.cm-3.
lation
length j(c)
and confirmsprevious
conventionallight scattering
data[27].
In the
regions
III andIII’,
the correlation function has been found to deviatesignificantly
fromsingle exponential
behaviour. Thedecay
time obtainedby
forcefitting
asingle exponential depends
on thesampling
time. On the otherhand,
the averagedecay
time determined from the cumulant
analysis
isinsensitive to a
change
of thesampling
time. Thesecond-order moment is of the order of
magnitude
of 0.2. We have not
attempted
arigorous analysis
of the correlation
function, using
the exactexpression given by
de Gennes and Dubois-Violette[28].
Suchan
analysis
has beenperformed by Adam, et
al.[10]
on the
system polystyrene-benzene.
Figure
4 shows the concentrationdependence
ofboth
Do
andDc
obtained from the data offigure
3.FIG. 4. - Semi-dilute solutions of linear PDMS samples in toluene.
+ Mw = 6 X 106; 0 Mn = 17 100;
x Mn = 4 500.The behaviour of the diffusion constant is
quite
different from that observed in other
polymeric systems
in many respects :- In the dilute
domain, Do
isindependent
of theconcentration.
- Within the
experimental
accuracy, theexponent
of the power lawDe
=f (c)
is thatpredicted by
thetheory
- There is
quite
asharp
transition between dilute and semi-dilutesolutions,
which defines with afairly good
accuracy the cross-over concentration c*. The concentrationcé p
at whichDo
=f (c)
andDc
=f(c)
intersect is found to be :
The cross-over concentration calculated from
(NA : Avogadro number)
is :In
figure
4 we have alsoplotted
the diffusionconstant as a function of concentration for PDMS of small molecular
weights.
In the dilute range,Do
variessignificantly
with c. In the semi-dilute range theexperimental points
lie on the same curveDe
=f (c)
as that for thehigh
molecularweight sample.
These datarepresent
the free diffusionconstant
D free
in thedisentangled regime (region II’),
since
they
have been obtained for a range of K values much smaller thanKmin
which can be calculated from[13] :
Typically
forc*/c
=1/2
and M = 17 100One can,
therefore,
conclude that for the systeminvestigated,
the diffusion constant follows the samescaling
law with the concentration in both thegel
andthe
disentangled regimes
withoutchange
of thenumerical value of the
prefactor.
4.2 PDMS NETWORKS SWOLLEN IN TOLUENE TO THEIR EQUILIBRIUM STATE. - 4. 2.1
Shape of
the auto-correlation
function.
- The resultsreported
inprevious
papers, related to thelight spectroscopy
ofpolystyrene
networks swollenby
benzene andethyl-
acetate, demonstrated the
validity
of thehydro- dynamic
model.On the other
hand,
the results of Wun and Carl-son on
polyacrylamide gels supported
the harmoni-cally
boundparticle
model[4].
Therefore we have
proceeded
to a careful investi-gation
of the autocorrelation function and of the Kdependence
of thedecay
rate for PDMS networks.We have found that the autocorrelation function
can be described
by
asingle exponential
with the samestatistical accuracy as for dilute solutions of mono-
disperse polymers.
The cumulantanalysis
leads toa value of
(P2/r2)
of about 0.02.The
decay
rate varies asK2
forscattering angles ranging
from 60 to 900. In this range, the scatteredsignal
isfully heterodyned by
theinhomogeneities present
in thesample,
as evidencedby experiments performed using
an external oscillator.4.2.2 The
cooperative diffusion
constant. - Theexperimental
values ofDc
for PDMS networks arelisted in table I.
Figure
5 shows the variation ofDc
as a function of the
polymer
concentration of thegel
swollen to
equilibrium.
The dataobey approximately
the same
scaling
law as the semi-dilutesolutions,
with a
change
of theprefactor
value. However aclose
inspection
offigure
5 shows that the data areFIG. 5. - Plot of De versus Ce for PDMS networks swollen in toluene. + f = 3 ; 0 f = 4 ; · f = 6. f refers to the functionality
of the crosslinking agent. The straight line represents De = f (c)
for semi-dilute solutions.
rather best accounted for
by fitting
the data of each seriesof
networks ofgiven functionality separately.
One obtains then three
slightly
shiftedstraight
linesof
slopes ranging
from 0.9 to 1.4.2.3 The
compressional
modulus. - The dataobtained
by Belkebir,
et al.[24]
forcompressional
modulus E of PDMS networks swollen in toluene
are listed in table I.
Figure
6 shows alog-log plot
of E versus the
equilibrium
concentration. The datacan be fitted
roughly
with twoslightly
shiftedstraight lines,
one linecorresponding
to thef6 networks,
the other one to the
f3 and f4
networks. Theslope
of these
straight
lines is about 4.5.FIG. 6. - Compressional modulus E versus ce. + f = 3 ; 01= 4 ; tbf = 6.
5. Discussion. - In the
following discussion,
weshall summarize the main results of our
study,
whichare
quite
different from those obtained onpolystyrene-
benzene systems in many respects, and we shall
attempt
aconjectural description
of thetopology
of the networks which is able to account for the
experimental
observations.a)
For semi-dilute solutions ofhigh
molecularweight
PDMS intoluene,
the exponent of thescaling
law
Dc
=f(c)
is ingood
agreement with thepredicted value, contrary
to the resultspreviously
obtainedin
polystyrene
systems. Thisobservation
may be related to the elastomeric nature of the PDMSchain,
which is much more flexible than that of the
polysty-
rene. An alternative
explanation
can be inferred from the rather poor solventquality
of the toluene forPDMS,
as shownby
the low value of the second virial coefficient(cf.
TableII),
which is of the sameorder of
magnitude
as that ofpolystyrene
incyclo-
hexane at a
temperature
ofapproximately
200 abovethe theta
temperature.
In thetasolvent,
the coherencelength
isproportional
to the concentration. It may bepossible
that the behaviour of PDMS solutions in toluene is intermediate between those of thetaregime
and
good
solventregime, resulting
in a value ofthe critical
exponent
between 0.67 and 1. Anunequi-
vocal answer would be
given by
astudy
of self-diffusion coefficient
Do
as a function of molecularweight
for a series ofmonodisperse samples
in dilutesolutions.
Indeed,
if the system PDMS-tolueneobeys
the
good
solventscaling
lawstheory,
thenDo
shouldvary
according
toMO.6.
Theexponent b
of the power lawDo
oc M - b can also be obtained from the expo- nent a in theviscosity
Mark-Houwinkequation [1]
oc Mathrough
therelationship [16] :
b =(a
+1)/3.
Values of b calculated from literature
viscosity
datarange from 0.57
[29]
to 0.61[30]
for PDMSsamples
of
high
molecularweights (>
20000)
in toluene.These results
give
strong evidence that in PDMS toluenesystems
one observesgood
solventbehaviour,
the values of criticalexponents being
thosepredicted by
thetheory.
On the otherhand,
for PDMS of low molecularweights (
20000)
the measured values of b range from 0.5[31]
to 0.53[24], indicating
poor solvent behaviour.b)
For swollen networks oneobserves,
in the firstapproximation,
ascaling
law forDc
=f(ce).
Thisresult,
which confirms thosepreviously
obtained frompolystyrene gels, implies
that the collective modes of networks swollen at theirequilibrium
state arealso controlled
by
the correlationlength j
associatedwith the
equilibrium
concentration Ce, Thereis, however,
asystematic upward
shift of the curveDc
=f(ce)
relative to thenetworks,
withrespect
to the
De
=f(c)
curve of the semi-dilute solutions.This shift may be attributed to a différence in the
equilibrium
conditions : swollen networks are studied in the presence of an excess of solvent and as a conse-quence the chemical
potential
of the solvent within the network is the same as that of the pure solvent.On the other